High strength galvanized steel sheet having excellent bendability and weldability, and method of manufacturing the same

ABSTRACT

A high strength galvanized steel sheet having excellent bendability and weldability, comprising by mass %: C: equal to or more than 0.05% and less than 0.12%; P: 0.001 to 0.040%; and S: equal to or less than 0.0050%, wherein a steel sheet surface layer, constituting a portion of the steel sheet up to a depth of 10 μm measured from each surface of the steel sheet, has a structure containing more than 70% of ferrite phase by a volume fraction, a steel sheet inner layer portion, on an inner side than the depth of 10 μm measured from each surface, has a structure containing 20 to 70% by a volume fraction of ferrite phase with an average crystal grain size equal to or smaller than 5 μm, the steel sheet has a tensile strength equal to or larger than 980 MPa, and the steel sheet has a galvanized layer on a surface thereof.

RELATED APPLICATIONS

This is a §371 of International Application No. PCT/JP2011/002999, withan international filing date of May 30, 2011 (WO 2011/152017 A1,published Dec. 8, 2011), which is based on Japanese Patent ApplicationNos. 2010-125306, filed May 31, 2010, and 2011-118173, filed May 26,2011, the subject matter of which is incorporated herein by reference.

TECHNICAL FIELD

This disclosure relates to a high strength galvanized steel sheet havingexcellent bendability and weldability with tensile strength (TS) of 980MPa or larger, which steel sheet is suited for use as an automobilecomponent to be subjected to severe bending process or the like, and amethod of producing the same.

The term “galvanized steel sheet” collectively refers to a so-called“galvannealed” steel sheet that has been subjected to alloy annealingtreatment subsequent to hot-dip galvanization.

BACKGROUND

A high strength galvanized steel sheet for use as an automobilecomponent or the like is required to have excellent workability as wellas high strength, due to the nature of its application.

Recently, as a vehicle body becomes increasingly lightweight in view ofimproving fuel efficiency, a high strength steel sheet is required to beused in an automobile body to ensure collision safety, and the scope ofapplication of such a high strength steel sheet is expanding. Further,although a high strength steel sheet is normally subjected to lightshaping in the conventional technique, it is now being studied to applythe high strength steel sheet to a complex shape.

However, the workability of a steel sheet generally deteriorates as thestrength thereof increases. Accordingly, when a high strength steelsheet is applied to a vehicle body, there arises a problem such asfracturing when the steel sheet is subjected to press forming. Inparticular, the aforementioned problem is likely to occur in applying ahigh strength steel sheet having a tensile strength of 980 MPa or largerto a component that is to be bent/formed.

Further, since vehicle body processing involves an assembly processsubsequent to press forming and it is necessary to perform resistancespot welding in the assembly process, excellent weldability is alsorequired along with workability.

To meet the above-mentioned requirements, for example, JP-A 2004-232011,JP-A 2002-256386, JP-A 2002-317245, JP-A 2005-105367, JP-B 3263143, JP-B3596316, and JP-A 2001-011538 each propose a method of obtaining a highstrength galvanized steel sheet with high workability by specifyingsteel components and structures or optimizing hot rolling condi-tionsand annealing conditions. Further, JP-A 02-175839, JP-A 05-195149, JP-A10-130782, JP-A 2005-273002, and JP-A 2002-161336 each disclose atechnology of obtaining a cold-rolled steel sheet excellent inbendability, JP-A 2006-161064 discloses a technology of obtaining a hightensile strength galvanized steel sheet excellent in bendability, andJP-A 2008-280608 discloses a technology of providing a galvanized steelsheet excellent in workability and weldability.

Among the above-cited publications, JP-A 2004-232011 describes a steelsatisfying a tensile strength of 980 MPa or so and having a high contentof C and Si. However, JP-A 2004-232011 gives no consideration toimprovement in stretch flangeability and bendability.

Similarly, JP-A 2002-256386, JP-A 2002-317245 and JP-A 2005-105367 eachdisclose a steel member that utilizes Cr, but gives no consideration toimprovement in stretch flangeability and bendability.

JP-B 3263143, JP-B 3596316, and JP-A 2001-011538 each refer to ductilityratio X, which is one of the indexes for evaluating stretchflangeability. However, the tensile strengths (TS) of steel sheets,subjected to the measurement of the ductility ratio, of thesepublications fail to reach 980 MPa. Further, these publications aresilent about bendability of the steel sheets thereof.

JP-A 02-175839, JP-A 05-195149, JP-A 10-130782, JP-A 2005-273002 eachdisclose a technology involving bendability of steel sheets by softeningthe steel sheets in regions measured from surfaces thereof in thethickness direction to a depth of at least 10 vol % or at least 10 μm.However, there arises a problem in that the soft layer in the steelsheet surface layer is so thick that fatigue strength deteriorates.

JP-A 2002-161336 describes that a steel sheet can be improved inbendability when a soft layer is formed in the steel sheet surface to adepth up to 10 μm. However, JP-A 2002-161336 fails to specify the steelsheet structure and thus inevitably faces a problem that fatiguestrength of the steel sheet decreases as a whole.

JP-A 2006-161064, although it discloses improving bendability of a steelsheet by setting the area ratio of a ferrite phase to be 80% or more invicinities of the top surfaces (a depth of 1 to 10 μm measured from thesurface layer) of the steel sheet, fails to make any reference to theinternal structure of the steel sheet. Further, JP-A 2006-161064 has nodescription of weldability and plane-bending fatigue properties of thesteel sheet, thereby still having a problem in terms of weldability andplane-bending fatigue properties.

JP-A 2008-280608 discloses a high strength galvanized steel sheetexcellent in workability and weldability, as well as bendability toattain a critical bend radius not larger than 1.5t (hereinafter, trepresents sheet thickness of the steel sheet) at 90° V-bending. JP-A2008-280608 has actually achieved a critical bend radius as small as0.36t. However, to further expand the scope of application of the highstrength steel sheet to a vehicle body, bendability needs to be furtherincreased, that is, critical bend radius needs to be further reduced.Specifically, critical bend radius not larger than 0.3t is required.

It could therefore be helpful to provide a high strength galvanizedsteel sheet having very good bendability and weldability, whichspecifically has high tensile strength of 980 MPa or larger andsatisfies a durability ratio, defined as fatigue limit/tensile strength,of 0.35 or larger without deteriorating the plane-bending fatigueproperty, as well as an advantageous production method of the steelsheet.

SUMMARY

The term “high strength” means tensile strength of 980 MPa or larger.Further, the expression that a steel sheet “has excellent bendability”means that a critical bend radius at 90° V-bending is not larger than0.3t. Yet further, the expression that a steel sheet “is excellent inweldability” means that a base material fracture occurs when a nuggetdiameter is 4t^(1/2) (mm) or larger.

We discovered that:

(1) Excellent weldability can be achieved by reducing contents of C, P,and S in a composition of a steel sheet components.(2) To improve bendability, it is effective to form the steel sheetsurface layer structure mainly of a ferrite phase, specifically, formmore than 70% by a volume fraction of the steel sheet surface layerstructure of a ferrite phase to soften the structure. In this case, thefatigue resistance property deteriorates due to the softening of thesteel sheet surface layer in turn.

However, if the thickness of the steel sheet surface layer formed mainlyof a ferrite phase is set not to exceed 10 μm or so, the aforemetionedadverse effect on fatigue resistance property can be suppressed whileachieving significant improvement in bendability.

(3) On the other hand, a steel sheet structure on the inner side thanthe steel sheet surface layer needs to include a ferrite phase to acertain extent, specifically, at least about 20% by a volume fraction toensure bendability. However, when the ferrite phase of the innerstructure exceeds 70%, the fatigue resistance property deteriorates,making it difficult to ensure the strength of 980 MPa or larger.

We thus provide:

1. A high strength galvanized steel sheet having excellent bendabilityand weldability, comprising by mass %: C: equal to or more than 0.05%and less than 0.12%; P: 0.001 to 0.040%; and S: equal to or less than0.0050%, wherein a steel sheet surface layer, constituting a portion ofthe steel sheet up to a depth of 10 μm measured from each surface of thesteel sheet, has a structure containing more than 70% of ferrite phaseby a volume fraction, a steel sheet inner layer portion, on the innerside than the depth of 10 μm measured from each surface, has a structurecontaining 20 to 70% by a volume fraction of ferrite phase with anaverage crystal grain size equal to or smaller than 5 μm, the steelsheet has a tensile strength equal to or larger than 980 MPa, and thesteel sheet has a galvanized layer on a surface thereof.2. The high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 1, wherein thestructure of the steel sheet inner layer portion contains: 20 to 70% offerrite phase by a volume fraction, with an average crystal grain sizeequal to or smaller than 5 μm; 30 to 80% of bainite phase and/ormartensitic phase by a volume fraction, with an average crystal grainsize of equal to or smaller than 5 μm; and residual austenite phaseand/or pearlite phase equal to or less than 5% (inclusive of 0%) by avolume fraction as the remainder.3. The high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 1 or 2, whereinthe steel sheet, further comprising by mass %: C: equal to or more than0.05% and less than 0.12%; P: 0.001 to 0.040%; S: equal to or less than0.0050%; Si: 0.01 to 1.6%; Mn: 2.0 to 3.5%; Al: 0.005 to 0.1%; N: equalto or less than 0.0060%; and the remainder as Fe and incidentalimpurities.4. The high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 3, furthercomprising by mass %: at least one element selected from the groupsconsisting of Cr: more than 0.5% and equal to or less than 2.0%, Mo:0.01 to 0.50%, and B: 0.0001 to 0.0030%; and the remainder as Fe andincidental impurities.5. The high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 3 or 4, furthercomprising by mass %: at least one element selected from the groupconsisting of Ti: 0.010 to 0.080% and Nb: 0.010 to 0.080%; and theremainder as Fe and incidental impurities.6. The high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 5, comprising bymass %: C: equal to or more than 0.05% and less than 0.12%; P: 0.001 to0.040%; S: equal to or less than 0.0050%; Si: 0.01 to 1.6%; Mn: 2.0 to3.5%; Al: 0.005 to 0.1%; N: equal to or less than 0.0060%; Cr: more than0.5% and equal to or less than 2.0%; Mo: 0.01 to 0.50%; Ti: 0.010 to0.080%; Nb: 0.010 to 0.080%; B: 0.0001 to 0.0030%; and the remainder asFe and incidental impurities.

Specifically, the steel sheet described in the above-mentioned item 6 isthe high strength galvanized steel sheet having excellent bendabilityand weldability according to the above-mentioned item 1 or 2,characteristically containing by mass %, C: equal to or more than 0.05%and less than 0.12%, P: 0.001 to 0.040%, S: equal to or less than0.0050%, Si: 0.01 to 1.6%, Mn: 2.0 to 3.5%, Al: 0.005 to 0.1%, N: equalto or less than 0.0060%, Cr: more than 0.5% and equal to or less than2.0%, Mo: 0.01 to 0.50%, Ti: 0.010 to 0.080%, Nb: 0.010 to 0.080%, andB: 0.0001 to 0.0030%, and the remainder as Fe and incidental impurities.

7. A method of manufacturing a galvanized steel sheet having excellentbendability and weldability by: subjecting a steel slab having acomposition according to any one of items 1 to 6 above to heating andhot rolling; winding up the hot-rolled steel into a coil; subjecting thesteel to pickling and cold rolling; and galvanizing the resulting steelsheet, the method comprising the steps of: subjecting the steel slab toheating at a temperature in the range of 1150 to 1300° C. and then hotrolling at a hot finishing rolling temperature in the range of 850 to950° C.; cooling the steel from the hot finishing rolling temperature to(the hot finishing rolling temperature minus 100° C.) at an averagecooling rate of 5 to 200° C./second; winding up the steel into a coil ata temperature of 400 to 650° C.; subjecting the steel to the picklingand the cold rolling; and subjecting the cold-rolled steel sheet toannealing including two-stage temperature raising processes, wherein theannealing step includes: primary heating of the steel sheet from 200° C.to an intermediate temperature in the range of 500 to 800° C. at aprimary average heating rate of 5 to 50° C./second at an excess airratio of 1.10 to 1.20 maintained up to the intermediate temperature;secondary heating of the steel sheet from the intermediate temperatureto an annealing temperature in the range of 730 to 900° C. at asecondary average heating rate of 0.1 to 10° C./second at an excess airratio of less than 1.10 maintained up to the annealing temperature;holding the steel sheet in the range of the annealing temperature for 10to 500 seconds; cooling the steel sheet to a temperature in the range of450 to 550° C. at an average cooling rate of 1 to 30° C./second; andsubjecting the steel sheet to a galvanizing process and optionally analloying process.

A high strength galvanized steel sheet which is effectively improved inbendability and weldability can be obtained. This high strengthgalvanized steel can satisfy both the strength and the workabilitynecessitated by an automobile component and thus can be suitably usedfor an automobile component which is to be press formed into a shaperequiring severe bending.

DETAILED DESCRIPTION

First, descriptions will be given for limiting compositions of thecomponents of the steel sheet to the above-mentioned ranges. “%”regarding a content of each component of the steel sheet represents“mass %” unless otherwise specified.

C: 0.05% or more and less than 0.12%

C is an indispensable element in terms of strengthening steel byutilizing a hard phase such as a martensitic phase or a bainite phase.0.05% or more of C is required to obtain a tensile strength (which willbe referred to as “TS” hereinafter) of 980 MPa or more. As the C contentincreases, TS increases accordingly. In a case where the C content is0.12% or more, not only spot weldability significantly deteriorates, butalso workability such as bendability tends to significantly deterioratedue to hardening caused by increase in the hard phase. The C content isthus to be limited to 0.05% or more and less than 0.12%. The C contentis more preferably 0.105% or less. In view of stably ensuring TS of 980MPa or larger, the C content is preferably 0.08% or more.

P: 0.001 to 0.040%

P is an element that contributes to improving strength and the contentthereof is 0.001% or more. However, the element P deterioratesweldability. Weldability improves when a steel sheet surface layerportion ranging from a surface of a steel sheet up to the 10 μm depth ofthe steel sheet, i.e., from an interface between the steel sheet and anzinc plating up to the 10 μm depth of the steel sheet (which surfacelayer portion will be referred to simply as a “steel sheet surface layerportion” hereinafter) contains ferrite by a volume fraction of 70% ormore. In a case where the P content exceeds 0.040%, P significantlycauses an adverse effect of deteriorating weldability. The P content istherefore to be limited to 0.001 to 0.040%, preferably 0.001 to 0.025%,and more preferably 0.001 to 0.015%.

S: 0.0050% or less

Weldability deteriorates as the S content increases. In particular, in acase where the S content exceeds 0.0050%, sulfur significantly causes aneffect of deteriorating weldability. Further, an increase in the Scontent not only causes red shortness and incurs problems such asfracture of a hot-rolled sheet, but also forms MnS as inclusions in asteel sheet, which remains as sheet-like inclusions after cold rollingto deteriorate ultimate deformability of the material or formabilitysuch as stretch flangeability. Therefore, the S content is preferably aslow as possible, although it may be tolerated up to 0.0050%. The Scontent is preferably 0.0030% or less. However, since excessivereduction of the S content results in increase in desulfurizing cost inthe steelmaking process, the lower limit of the S content is preferablyabout 0.0001%.

Contents of C, P, and S are specified as described above to attainexcellent weldability. It is effective to include, for example, Si, Mn,or Al in the steel sheet to obtain desired characteristics, inparticular, to improve strength and weldability. Further, to improve thequench hardenability, it is also effective to add one or more elementsselected from among Cr, Mo, and B in a predetermined content. Yetfurther, one or two elements selected from Ti and Nb can be added in apredetermined content as an element capable of facilitatingprecipitation, to further improve bendability. For the reasons describedabove, it is preferable to appropriately include, Si: 0.01 to 1.6%, Mn:2.0 to 3.5%, Al: 0.005 to 0.1%, Cr: more than 0.5% and 2.0% or less, Mo:0.01 to 0.50%, Ti: 0.010 to 0.080%, Nb: 0.010 to 0.080%, and B: 0.0001to 0.0030%, respectively. It is preferable to limit the content of N to0.0060% or less because an increase in content of N significantlyaffects ductility of the steel sheet as described below.

Si: 0.01 to 1.6%

Si is an element that contributes to improving strength and bendabilityof the steel sheet through solid solution strengthening. However, the Sicontent needs to be 0.01% or more to cause a good effect of Si addition.However, in a case where the Si content exceeds 1.6%, Si is concentratedas an oxide on the steel sheet surface, causing plating failure. The Sicontent is therefore preferably 0.01 to 1.6%. The Si content is morepreferably 0.8% or less, further more preferably less than 0.35%, andmost preferably 0.20% or less to avoid plating failure. Mn: 2.0 to 3.5%

Manganese effectively contributes to improving strength and this effectis recognizable when the Mn content is 2.0% or more. In a case where theMn content exceeds 3.5%, the structure suffers from localized variationin transformation point due to segregation of Mn or the like. As aresult, the steel sheet has a non-uniform structure in which a ferritephase and a martensitic phase exist in the form of bands, resulting inpoor bendability. Further, in this case, Mn is concentrated as an oxideon the steel sheet surface, causing plating failure. The Mn content isthus 2.0 to 3.5%, preferably 2.2 to 2.8%.

Al: 0.005 to 0.1%

Al is an element which is effective as a deoxidizing agent in thesteelmaking process and also useful for separating a non-metal inclusionwhich would deteriorate bendability away into slag. Further, Al has afunction of suppressing generation of Mn/Si-oxides, which wouldadversely affect plating properties during annealing and thus improveappearance of a plating surface. The Al content needs to be 0.005% ormore to obtain such good effects. In a case where the Al content thusadded exceeds 0.1%, not only the steelmaking cost is increased but alsoweldability deteriorates. The Al content is therefore 0.005 to 0.1%, andpreferably 0.01 to 0.06%.

N: 0.0060% or less

To improve ductility by making ferrite clean, the N content ispreferably as low as possible. In particular, in a case where the Ncontent exceeds 0.0060%, ductility is significantly deteriorated.Therefore, the upper limit of the N content is to be 0.0060%. The lowerlimit of the N content is preferably 0.0001% or so in view of therefining cost. In short, the N content is to be 0.0060% or less, andpreferably in the range of 0.0001 to 0.0060%.

Cr: more than 0.5% and 2.0% or less

Cr is an element which is effective in facilitating quench hardening ofsteel. Cr also improves quench hardenability of an austenite phase,makes a hard phase extend uniformly such that the hard phase is finelydispersed, and effectively contributes to the improvement in stretchflangeability and bendability. The Cr content needs to be more than 0.5%to cause a good effect of Cr addition. However, in a case where the Crcontent exceeds 2.0%, this good effect reaches a plateau and the surfacequality rather deteriorates. The Cr content is therefore more than 0.5%and 2.0% or less, and preferably more than 0.5% and 1.0% or less.

Mo: 0.01 to 0.50%

Mo is an element which is effective in facilitating quench hardening ofsteel. A very small amount of Mo added to a low-carbon steel componentsystem readily ensures good strength of steel. Further, Mo causes aneffect of improving weldability and bendability. The Mo content needs tobe 0.01% or more to cause the good effect of Mo addition. In a casewhere the Mo content exeeds 0.50%, the good effect reaches a plateau andthe production cost may rise up. The Mo content is thus 0.01 to 0.50%and preferably 0.01 to 0.35%.

Ti: 0.010 to 0.080%

Ti reacts with C or N in steel to form a fine carbide or a fine nitride,to thereby grain-refine a hot rolled sheet structure and a steel sheetstructure after annealing to improve bend-ability, and also effectivelyfacilitate precipitation. The Ti content needs to be 0.010% or more tocause a good effect. In a case where the Ti content exceeds 0.080%, thisgood effect reaches a plateau and an excessive amount of precipitates isgenerated in ferrite, which deteriorates ductility of ferrite. The Ticontent is 0.010 to 0.080%, and preferably 0.010 to 0.060%. Nb: 0.010 to0.080%

Nb is an element that contributes to improving strength of a steel sheetby facilitating solid solution or precipitation. Nb also has an effectof strengthening the ferrite phase to reduce the difference in hardnessbetween the ferrite and martensitic phases, to thereby effectivelycontribute to improving stretch flangeability. Further, Nb contributesto grain-refining of ferrite grains and crystal grains in thebainite/martensitic region, thereby improving bendability. The Nbcontent needs to be 0.010% or more to cause a good effect of Nbaddition. In a case where the Nb content exceeds 0.08%, the hot-rolledsheet is hardened, which results in an increase in rolling load duringhot rolling or cold rolling. Further, in this case, ductility of ferritedeteriorates and workability is impaired. The Nb content is thus 0.010to 0.080%. In view of achieving good strength and workability, the Nbcontent is preferably 0.030 to 0.070%.

B: 0.0001 to 0.0030%

Boron contributes to improving quench hardenability, suppressinggeneration of ferrite which occurs in the annealing cooling process, andobtaining a desired amount of the hard phase, to thereby improvebendability. The B content needs to be 0.0001% or more to cause a goodeffect. In a case where the B content exceeds 0.0030%, the good effectreaches a plateau. The B content is therefore 0.0001 to 0.0030% andpreferably 0.0005 to 0.0020%.

Specifically, a particularly preferable example of an elementcomposition is as follows:

-   -   (1) A composition containing C: 0.05% or more and less than        0.12%, P: 0.001 to 0.040%, S: 0.0050% or less, Si: 0.01 to 1.6%,        Mn: 2.0 to 3.5%, Al: 0.005 to 0.1%, and N: 0.0060% or less, and        Fe and incidental impurities as the remainder.    -   (2) A composition containing, in addition to the composition        of (1) above, one or more elements selected from the group        consisting of Cr: more than 0.5% and 2.0% or less, Mo: 0.01 to        0.50%, and B: 0.0001 to 0.0030%. (3) A composition containing,        in addition to the composition of (1) or (2) above, one or two        elements selected from Ti: 0.010 to 0.080% and Nb: 0.010 to        0.080%.

The most preferable example of an element composition is as follows:

-   -   A composition containing C: 0.05% or more and less than 0.12%,        P: 0.001 to 0.040%, S: 0.0050% or less, Si: 0.01 to 1.6%, Mn:        2.0 to 3.5%, Al: 0.005 to 0.1%, N: 0.0060% or less, Cr: more        than 0.5% and 2.0% or less, Mo: 0.01 to 0.50%, Ti: 0.010 to        0.080%, Nb: 0.010 to 0.080%, B: 0.0001 to 0.0030%, and Fe and        incidental impurities as the remainder.

The element composition may further optionally contain followingelements in an appropriate manner. Ca causes an effect of improvingductility by shape control of a sulfide such as MnS. If the Ca contentincreases too much, the effect tends to reach a plateau. In view ofthis, when Ca is contained, the content thereof is 0.0001 to 0.0050% andmore preferably 0.0001 to 0.0020%.

Further, Vanadium has an effect of strengthening a ferrite phase throughformation of carbide. However, a too large V content rather deterioratesductility of the ferrite phase. The V content is therefore preferably0.001% or more and less than 0.05% and more preferably 0.001% or moreand less than 0.005%.

Further, it is preferable that the element composition includes REMcapable of controlling sulfide inclusion morphology withoutsignificantly changing plating properties to thereby effectivelycontribute to improving workability, or Sb capable of rendering crystalgrains of a steel sheet surface layer uniform by a content of 0.0001 to0.1%, respectively.

Contents of other elements such as Zr, Mg which would form precipitatesare preferably as low as possible. Therefore, it is not necessary tointentionally add these elements. The contents of these other elementsare tolerated up to less than 0.0200% and preferably less than 0.0002%.

Cu and Ni are elements that adversely affect weldability and appearanceof a galvanized surface, respectively. The Cu and Ni contents aretolerated up to less than 0.4% and preferably less than 0.04%.

In the steel sheet, the remainder other than the aforementionedcomponent elements is preferably constituted of Fe and incidentalimpurities.

Next, descriptions will be given of appropriate content ranges regardinga steel structure, which are critical requirements, as well as thereasons for specifying the ranges as such.

Structure having a steel sheet surface layer portion containing morethan 70% by volume fraction of ferrite phase

Bendability of a steel sheet can be improved by designing a structure ofa steel sheet surface layer portion as a structure mainly constituted ofa ferrite phase. This effect cannot be obtained when the volume fractionof the ferrite phase is 70% or less. Accordingly, the volume fraction ofthe ferrite phase in the steel sheet surface layer portion is to be morethan 70%, and preferably equal to or more than 85%.

Observation of a structure of the steel sheet is carried out by:photographing a surface parallel to the rolling direction of the steelsheet by using a scanning electron micrograph (SEM) at an appropriatemagnification of about 1,000 to 3.000-fold magnification; selectingthree arbitrary sites in a steel sheet surface layer portion in thephotography thus obtained; and calculating a volume fraction of ferriteor the like in these sites.

In the high strength galvanized steel sheet, an inner layer portion ofthe steel sheet, located deeper than 10 μm measured from the steel sheetsurface, has a structure containing at least 20 to 70% volume fractionof a ferrite phase with an average crystal grain size of 5 μm or less.

A structure of a portion of a steel sheet, located on the inner side ofa steel sheet surface layer up to the center in thickness direction ofthe steel sheet, which portion will be referred to as a “steel sheetinner layer portion” hereinafter, is specifically represented by astructure of a region located in the depth range of 10 to 50 μm withthickness of 40 μm and a structure of a region of 40 μm thicknesslocated at the ¼ sheet thickness position measured from the surface. Thestructures at both positions are observed, and in a case where a ferritephase with the average crystal grain size of 5 μm or less exists at 20to 70% volume fraction at both of the positions, it is determined thatthe steel sheet inner layer portion satisfies the above-mentionedstructure. Specifically, SEM images of the structures of a regionlocated from the 10 μm depth to the 50 μm depth measured from the steelsheet surface or the steel sheet/zinc plating interface toward thecenter of the steel sheet (a region extending by 40 μm in the depthdirection and by 20 μm in the rolling direction); and a region locatedat a position of the ¼ sheet thickness (a region extending by 40 μm inthe depth direction and by 20 μm in the rolling direction) are taken,respectively, at an appropriate magnification of about 1,000 to3.000-fold magnification, for a surface in the rolling direction of thesteel sheet, and three arbitrary points are observed for analysis.

Volume fraction of ferrite phase: 20 to 70% (Steel sheet inner layer)

A ferrite phase is a soft phase and contributes to ductility of a steelsheet. Hence, the structure of the steel sheet inner layer needs tocontain 20% or more of a ferrite phase by a volume fraction. In a casewhere the volume fraction of the ferrite phase exceeds 70%, the steelsheet is excessively softened, making it difficult to ensure sufficientstrength and good plane-bending fatigue property of the steel sheet. Thevolume fraction of a ferrite phase is therefore to be 20 to 70%,preferably in the range of 30 to 50%.

Average crystal grain Size of ferrite phase: 5 μm or less (Steel sheetinner layer)

Grain refining of crystal grains contributes to improvement inductility, stretch flangeability, and bendability of a steel sheet. Inview of this, in the steel sheet inner layer, the average crystal grainsize of a ferrite phase in a multi phase structure is limited to 5 μm orless, to thereby improve bendability. In a case where the averagecrystal grain size of the ferrite phase exceeds 5 μm, a desiredplane-bending fatigue cannot be ensured.

Further, if a soft region and a hard region are formed in a localizedmanner, the steel sheet is deformed non-uniformly, leading todegradation in bendability. In contrast, in a case where a soft ferritephase and a hard martensitic phase are uniformly and finely formed, thesteel sheet can be uniformly deformed during processing. The averagecrystal grain size of a ferrite phase is therefore preferably as smallas possible. The average crystal grain size of a ferrite phase ispreferably in the range of 1 to 3.5 μm to well suppress deterioration ofbendability of a steel sheet.

Other aspects of the steel sheet structure than the ferrite phase in thesteel sheet inner layer portion can be configured as follows.

Volume fraction of bainite phase and/or martensitic phase: 30 to 80%

A bainite phase and/or a martensitic phase are hard phases,respectively, and each have a function of increasing strength of thesteel sheet through structure reinforcement by transformation. Contentsof the bainite phase and/or the martensitic phase are preferably 30% ormore by a volume fraction to attain TS of 980 MPa or larger. The volumefraction of these phases is preferably 80% or less to obtain a desiredbendability.

Average crystal grain size of bainite phase and/or martensitic phase: 5μm or less

Grain refining of a bainite phase and/or a martensitic phase improveshole expansion properties, bendability, and plane-bending fatigue of thesteel plate. In this regard, desired properties can be attained bysetting the average crystal grain size of a bainite phase and amartensitic phase in a multi phase structure at 5 μm or less, preferably3 μm or less, in particular.

Possible structural aspects other than the aforementioned ferrite phase,martensitic phase and bainite phase in the steel sheet inner layerportion are residual austenite phase or a pearlite phase. The residualaustenite phase and/or the pearlite phase do not adversely affect aslong as the content thereof is 5% or less (including 0%) by a volumefraction.

Next, descriptions will be given of a preferable method of producing ahigh strength galvanized steel sheet.

First, a slab is manufactured through, for example, a continuous castingprocess or an ingot-making and blooming process from molten steelprepared to have an element composition. Then, the slab thus obtained issubjected to a series of processes in which the slab is either cooled,reheated and hot rolled or hot rolled immediately after the castingprocess skipping a heating process. In a case where the slab isreheated, the slab heating temperature is 1,150 to 1,300° C. to attainuniform structure of the hot rolled sheet and the finishing rollingtemperature in hot rolling 850 to 950° C. to improve workability such asductility and stretch flangeability, so that formation of a structure inwhich a ferrite phase and a pearlite phase exist in two bands-likeconfiguration is suppressed.

Further, the hot rolled steel is cooled from the hot finishing rollingtemperature by 100° C. at an average cooling rate of 5 to 200°C./second, and a coiling temperature at which the hot rolled steel iswound into a coil is adjusted to 400 to 650° C. to improve the surfacequality and easiness of cold rolling of the steel sheet, to therebycomplete hot rolling. Then, the steel cold rolled, after pickling, intoa desired thickness. The cold rolling reduction rate at this stage ispre-ferably 30% or more to facilitate recrystallization of a ferritephase to thereby improve ductility.

Next, prior to subjecting the steel sheet to a galvanizing process, thesteel sheet is subjected to annealing that undergoes two-stagetemperature raising processes. Structures of the surface layer portionand the inner layer portion of the steel sheet are controlled,respectively, by this annealing including two-stage temperature raisingprocesses. Specifically, an average rate of primary heating from 200° C.to an intermediate temperature in the range of 500 to 800° C. is to be 5to 50° C./second, and an average rate of secondary heating from theintermediate temperature to the annealing temperature in the range of730 to 900° C. is to be 0.1 to 10° C./second. The steel sheet is thenmaintained at the annealing temperature in the aforementioned range for10 to 500 seconds and cooled to a cooling stop temperature in the rangeof 450 to 550° C. at an average cooling rate of 1 to 30° C./second.

In the above-mentioned processes, the structure of the steel sheetsurface layer portion is adjusted in a state where an excess air ratioin the annealing furnace during the primary heating is 1.10 to 1.20. Anexcess air ratio in the annealing furnace during the secondary heatingis to be less than 1.10.

Subsequent to cooling, the steel sheet is dipped in a molten zinc bath.The coating weight of zing plating is then controlled by gas wiping orthe like. The steel sheet is then optionally heated for alloyingtreatment and cooled to a room temperature.

A high strength galvanized steel sheet can be obtained as describedabove. The galvanized steel sheet may further optioanally be subjectedto skinpass rolling.

An appropriate ranges of the relevant production conditions and thereason for such restrictions will be described further in detail below.

Slab Heating Temperature: 1,150 to 1,300° C.

Precipitates existing at the stage of heating a steel slab result incoarse precipitates in a steel sheet as a final product. These coarseprecipitates do not contribute to improving strength, but may rathermake it difficult to achieve a uniform structure of the hot rolledsheet. Therefore, it is necessary to remelt the precipitates depositedduring casting. In this regard, the heating at a temperature of 1,150°C. or more can solve even Ti/Nb-precipitates, for example. Further,reheating the steel sheet to 1,150° C. or more is useful in view ofscaling off defects such as blow holes and segregation in the slabsurface layer and reducing cracking and irregularities at a surface ofthe steel sheet surface, to obtain a smooth steel sheet surface.However, heating at a temperature higher than 1,300° C. causes coarsegrowth of austenite grains in the steel sheet structure, which resultsin a coarse structure of the final product and poor ductility thereof.Accordingly, the slab heating temperature is 1,150 to 1,300° C.

Finishing rolling temperature: 850 to 950° C.

Bendability (ductility, stretch flangeability) can be significantlyimproved by setting the finishing rolling temperature during in hotrolling at 850° C. or higher. In a case where the temperature fallsshort of 850° C., crystals which have been subjected to hot rolling haveprocessed or wrought structures, whereby ductility of the steel sheetdeteriorates. Further, if Mn, which acts as an element for stabilizingaustenite, is segregated in a cast piece, the transformation point ofAr₃ in the region is lowered and the austenite range expands to arelatively low temperature, whereby (in the case where finishing rollingtemperature is below 850° C.) the unrecrystallized temperature range andthe rolling end temperature fall within the same temperature range andunrecrystallized austenite eventually remains during hot rolling.Uniform deformation of the material during processing is inhibited andit is difficult to obtain excellent bendability in such a non-uniformstructure.

On the other hand, in a case where the finishing rolling temperatureexceeds 950° C., the production of oxide (scale) rapidly increases,whereby the interface between the base metal and the oxide is roughenedand the surface quality after pickling and cold rolling tends todeteriorate. In this case, if a portion of the hot rolling scale failsto be removed and remains as residue after pickling, the residue willadversely affect weldability in resistance spot welding. Further, inthis case, the crystal grain size may grow excessively coarse, therebycausing surface roughness in a pressed product during a forming process.Accordingly, the finishing rolling temperature is 850 to 950° C., andpreferably 900 to 930° C.

Average cooling rate between finishing rolling temperature and(Finishing rolling temperature minus 100° C.): 5 to 200° C./second

In a case where the cooling rate in a high temperature range immediatelyafter the finishing rolling (finishing temperature to (finishingtemperature minus 100° C.)) is lower than 5° C./second, a steel sheetafter hot rolling experiences recrystallization and grain growth, whichleads to a coarse structure of the hot rolled sheet structure in whichferrite and pearlite are formed in layers to exhibit a layeredbands-like structure. In a case where such a layered bands-likestructure is formed in a steel sheet before annealing, the steel sheetis subjected to a heating process in a state where densities ofcomponents thereof are not uniform, which makes it difficult tograin-refine and uniformalize the structure of the steel sheet in a heattreatment in the galvan-izing process. As a result, the steel sheetstructure to be finally obtained is non-uniform, exhibiting deterioratedductility and bendability. The average cooling rate in a range of(finishing temperature to (finishing temperature minus 100° C.)) istherefore to be equal to or higher than 5° C./sec. In a case where theaverage cooling rate in the range of (finishing temperature to(finishing temperature minus 100° C.)) exceeds 200° C./second, theeffect of the cooling reaches a plateau and rather causes a disadvantagein cost such as a need for a cooling device exclusively for this coolingprocess. The average cooling rate in a range of (finishing temperatureto (finishing temperature minus 100° C.)) is 5 to 200° C./second, andpreferably 20 to 100° C./second.

Winding temperature: 400 to 650° C.

In a case where the coiling temperature when the steel sheet thus rolledis wound exceeds 650° C., hot rolling scale thickness increases, wherebya steel surface after cold rolling is roughened with irregularitiesformed thereon and ferrite crystal grain size grow coarse, resulting inpoor bendability of the steel sheet. In this case, if a portion of thehot rolling scale fails to be removed and remains as residual afterpickling, the residual adversely affects weldability in resistant spotwelding. In a case where the coiling temperature is lower than 400° C.,strength of the hot rolled sheet is increased, whereby rolling road tobe exerted on the steel sheet in the cold rolling process increases andproductivity deteriorates. Accordingly, the coiling temperature is 400to 650° C., and preferably 450 to 600° C.

-   -   Primary average heating rate (from 200° C. to an intermediate        temperature): 5 to 50° C./second,    -   Air ratio in furnace at primary heating: 1.10 to 1.20,    -   Intermediate Temperature: 500 to 800° C.

In a case where the primary average heating rate during annealing priorto the start of galvanization is lower than 5° C./second, the steelsheet experiences coarse growth of crystal grains, which leads todeterioration in ductility and bendability. Although there is noparticular upper limit of the primary average heating rate, if the rateexceeds 50° C./second, the effect caused by the cooling reaches aplateau. Accordingly, the primary average heating rate is 5 to 50°C./second, preferably 10 to 50° C./second, and more preferably 15 to 30°C./second.

In a case where the intermediate temperature between the primary heatingand the secondary heating exceeds 800° C., not only the steel sheetexperiences coarse growth of the crystal grains and bendability of thesteel sheet deteriorates, but also a volume fraction of a ferrite phasein a structure of the steel sheet surface layer portion increases,leading to deterioration in fatigue property. In a case where theintermediate temperature is lower than 500° C., the effect caused by theprimary heating reaches a plateau, eliminating difference in volumefraction of a ferrite phase between the steel sheet surface layerportion and the steel sheet inner layer of a finally obtained product.Accordingly, the intermediate temperature is 500 to 800° C. Theintermediate temperature is preferably to be a temperature lower thanannealing temperature by about 200° C.

An excess air ratio in an annealing furnace during the above-mentionedprimary heating is generally set at 1.00 or less. However, the excessair ratio in the furnace during the primary heating is 1.10 to 1.20. Bysetting the excess air ratio in the furnace during the primary heatingto be 1.10 to 1.20 as described above, the structure of the steel sheetsurface layer portion can successfully contain more than 70% of aferrite phase, which is the most critical feature.

If the excess air ratio in the furnace during the primary heatingexceeds 1.20, the volume fraction of the ferrite phase also increases inthe steel sheet inner layer portion, which results in degradation of thefatigue property of the steel sheet. In a case where the excess airratio is less than 1.10, the volume fraction of ferrite in the steelsheet surface layer portion cannot exceed 70% as in the above-mentionedcase of the conventional excess air ratio, whereby bendability fails toimprove. The excess air ratio is preferably to fall to 1.12 to 1.17.

An excess air ratio represents a ratio of an amount of air in anannealing furnace with respect to a minimum amount of air required forcomplete combustion of combustible element, which minimum amount of airis obtained from chemical reactions associated with the completecombustion. Accordingly, the excess air ratio 1.00 means that theatmosphere in the furnace contains an amount of air equivalent to theamount of theoretical air. An excess air ratio exceeding 1.00 representsthat the atmosphere in the furnace contains an amount of air excessivefor complete combustion of the combustible element. An excess air ratioof less than 1.00 means that the atmosphere in the furnace cannot causecomplete combustion of the combustible element.

By setting the excess air ratio in the furnace during primary heatingduring annealing prior to the start of galvanization in theaforementioned range, a volume fraction of a ferrite phase can beeffectively increased to exceed 70% only in a structure in the steelsheet surface layer portion. Although the mechanism of this phenomenonhas not been elucidated yet, we believe it is as follows.

Namely, under a condition of a relatively high excess air ratio, Fe on asteel sheet surface is oxidized to generate Fe oxide and 0 in the Feoxide binds to C in the steel so that the solid solution of carbon isreduced. As a result, the volume fraction of ferrite increases only inthe structure of the steel sheet surface layer portion.

-   -   Secondary average heating rate (from the intermediate        temperature to the annealing temperature): 0.1 to 10° C./second,    -   Air ratio in furnace at secondary heating: less than 1.10

In a case where the secondary average heating rate during annealingprior to the start of galvanization is higher than 10° C./second,generation of an austenite phase is delayed, which increases the volumefraction of an eventually obtained ferrite phase, making it difficult toensure sufficient strength of the steel sheet. In a case where thesecondary average heating rate is lower than 0.1° C./second, crystalgrain size grows coarse, resulting in deterioration of ductility andbendability. The secondary average heating rate is 0.1 to 10° C./second,and preferably 0.5 to 5° C./second.

The excess air ratio in the furnace during the secondary heating is lessthan 1.10. In a case where the excess air ratio in the furnace duringthe secondary heating is 1.10 or higher, the volume fraction of aferrite phase exceeds 70% in the steel sheet inner layer portion locateddeeper than the 10 μm depth measured from the steel sheet surface layer,as well, thereby deteriorating fatigue property of the steel sheet.

The excess air ratio in a furnace during the secondary heating can beset to be equal to or less than 1.00, which is an ordinary excess airratio. The subsequent annealing process can be performed under an excessair ratio falling within this ordinary range, preferably 0.60 to 0.95.

Annealing temperature: 730 to 900° C., Retention time: 10 to 500 seconds

In a case where the annealing temperature prior to the start ofgalvanization is lower than 730° C., a sufficient amount of austenite isnot generated during annealing, whereby the steel sheet cannot reliablyhave sufficient strength. In a case where the annealing temperature ishigher than 900° C., the austenite phase grow coarse during heating,which leads to decrease in amount of ferrite generated in the subsequentcooling process and deterioration of bendability of the steel sheet.Further, in this case of relatively high annealing temperature, thecrystal grain size of a steel sheet structure eventually obtained tendsto be large, as a whole, thereby deteriorating both ductility andbendability. The annealing temperature is therefore 730 to 900° C.,preferably 750 to 850° C.

Further, in a case where the retention time is less than 10 seconds inthe above-mentioned annealing temperature range, the amount of austenitephase generated during annealing is insufficient, making it difficult toensure sufficient strength of a steel sheet as a final product. In acase where the steel sheet is subjected to annealing for a relativelylong time, crystal grains of a steel sheet structure tend to growcoarse. In particular, in a case where the retention time exceeds 500seconds, crystal grain sizes of an austenite phase and a ferrite phaseduring thermal annealing are excessively gross, whereby bendability of asteel sheet structure obtained after the thermal processingdeteriorates. Further, such gross or coarse austenitic grain size is notpreferable because a steel sheet surface may be roughened during thepress forming process. Yet further, such coarse austenitic and ferritegrain sizes lead to a decreased amount of ferrite phase generated in thecooling process to the cooling stop temperature, deterioratingductility, as well.

Accordingly, to both achieve to attain a more precisely nano-constructedstructure and obtain a uniform and fine structure by reducing aninfluence caused by the structure prior to annealing, the retention timeis 10 to 500 seconds, and preferably 20 to 200 seconds.

-   -   Average cooling rate from annealing temperature to cooling stop        temperature: 1 to 30° C./second,    -   Cooling stop temperature: 450 to 550° C.

The average cooling rate when the steel sheet is cooled to the coolingstop temperature plays an important role to controllably adjust anabundance ratio of a relatively soft ferrite phase with respect to arelatively hard bainite phase and/or martensitic phase so that the steelsheet has strength TS in a class of at least 980 MPa while retaininggood workability. Specifically, in a case where the average cooling rateexceeds 30° C./second, generation of a ferrite phase during cooling issuppressed while bainite and martensitic phases are excessivelygenerated, which ensures easily attaining TS in a class of 980 MPa, butcauses deterioration of bendability.

On the other hand, in a case where the average cooling rate is lowerthan 1° C./second, the amount of a pearlite phase as well as the amountof ferrite phase, generated in the cooling process, is increased,whereby a high TS value cannot be ensured. Accordingly, the averagecooling rate when the steel sheet is cooled to the cooling stoptemperature is 1 to 30° C./second, preferably 5 to 20° C./second, andmore preferably 10 to 20° C./second.

The method of cooling the steel sheet is preferably the conventional gascooling method. Other examples of the cooling method include anyconventional method such as a furnace-cooled method, a mist coolingmethod, a roll cooking method, a water cooling method and the like,which may also appropriately combined.

In a case where the cooling stop temperature is higher than 550° C., thesteel sheet structure is transformed from an austenite phase to apearlite phase or a bainite phase which are softer than a martensiticphase, whereby it is difficult to ensure a TS value in a class of 980MPa. In this case, a hard residual austenite phase may be generated, butthis cannot be a help because stretch flangeability is thendeteriorated. In a case where the cooling stop temperature is less than450° C., a residual austenite phase is increased due to progress ofbainite transformation, making it difficult to ensure TS in a class of980 MPa and deteriorating bendability of the steel sheet.

After the cooling is stopped as described above, the steel sheet issubjected to a hot-dip galvanizing treatment, whereby a galvanized steelsheet is obtained. After the aforementioned hot-dip galvanizingtreatment, the galvanized steel sheet is further optionally subjected toan alloying treatment of reheating it by using an induction heatingdevice or the like, to thereby obtain a galvannealed steel sheet.Conditions for the hot-dip galvanizing treatment and the alloyingtreatment for the steel sheet are not specifically limited and may bethe conventionally-known conditions.

A coating weight of hot-dip zinc plating is preferably about 20 to 150g/m² per one surface. In a case where the coating weight is less than 20g/m², it is difficult to ensure sufficient corrosion resistance of aproduct. In a case where the coating weight exceeds 150 g/m², thecorrosion resisting effect by zinc plating reaches a plateau and ratherthe production cost disadvantageously increases. The coating weight ofzinc plating is thus preferably 30 to 70 g/m².

After the continuous annealing, the galvannealed steel sheet as a finalproduct may be subjected to skinpass rolling for the purpose of shapecorrection and surface roughness adjustment. However, it should be notedthat excessive skinpass rolling introduces too much deformation to thesteel sheet, resulting in a roll-processed structure including wroughtcrystal grains and thus poor ductility. The rolling reduction rate inthe skinpass rolling is therefore preferably about 0.1 to 1.5%.

Example

Steel samples having element compositions shown in Table 1 were preparedby casting, respectively. These samples were subjected to slab heating,hot rolling, winding, cold rolling at a rolling reduction rate of 50%,continuous annealing, and galvanizing under conditions shown in Tables2-1 and 2-2, to thereby produce a galvanized steel sheet and agalvannealed steel sheet each having thickness of 2.0 mm and coatingweight of 45 g/m² per one surface. A rolling reduction rate during thecold rolling was set at 50% for all of the samples. Regarding the excessair ratio in a furnace during continuous annealing, the excess air ratioduring the primary heating was set as shown in Tables 2-1 and 2-2 andthe excess air ratio during the secondary heating and thereafter was setin the range of 0.8 to 1.0.

Each of the galvanized steel sheets and the galvannealed steel sheetswas subjected to material tests described below and material propertiesthereof were investigated. The results are shown in Tables 3-1, 3-2, and4.

The material tests and an evaluation method of material properties areas follows.

(1) Steel Sheet Structure

On a surface in parallel to the rolling direction of each steel sheetsample, SEM images of structures of a steel sheet surface layer portion,a steel sheet inner layer portion (a region located from the 10 depth tothe 50 μm depth measured from the steel sheet surface) and another steelsheet inner layer portion (a region located at the ¼ sheet thicknessposition) are photographed, respectively, at a magnification in therange of about 1,000 to 3.000-fold magnification. A volume fraction ofthe steel sheet structure is determined by using these SEM images thusobtained.

Specifically, the structures of the steel sheet inner layer portions aredetermined by observing: a structure of a region located from the 10 μmdepth to the 50 μm depth measured from the steel sheet surface or thesteel sheet/zinc plating interface toward the center of the steel sheet(a region extending by 40 μm in the depth direction and by 20 μm in therolling direction); and a region located at a position of the ¼ sheetthickness (a region extending by 40 μm in the depth direction and by 20μm in the rolling direction), respectively.

Regarding the average crystal grain size of a ferrite phase, crystalgrain size of the ferrite phase is measured according to the methodspecified in JIS G 0552: 1998 and the crystal grain size thus obtainedis converted into the average crystal grain size. Further, volume ratiosof a ferrite phase and a pearlite phase are acquired by: visuallyspecifying a ferrite phase and a pearlite phase by using a photographicimage of a sectional structure of a steel sheet at a 1.000-foldmagnification; obtaining area values occupied by the ferrite phase andthe pearlite phase through image analysis, respectively; and dividingthe area values thus obtained by a value of the analyzed area (the areaof the sectional structure image), respectively, to thereby calculatevolume fractions of the ferrite phase and the pearlite phase.

An amount of residual austenite is calculated by: grinding a steel sheetto be analyzed to the ¼ sheet thickness position thereof; polishing by0.1 mm the steel sheet thus ground, by chemical polishing to obtain apolished surface; analyzing the polished surface by Mo Kα beam from anX-ray diffractometer to measure integrated intensities of a (200) face,a (220) face, and a (311) face of fcc iron and a (200) face, a (211)face, and a (220) face of bcc iron, respectively; and obtaining afraction (i.e., a volume fraction) of the residual austenite from thesemeasured values.

In a steel structure of the steel sheet, the rest of the structure,other than the ferrite phase, the austenite phase, and the pearlitephase, is formed of a bainite phase and/or a martensitic phase.Therefore, the total amount of the bainite phase and the martensiticphase is regarded as the remaining portion other than the ferrite phase,the austenite phase, and the pearlite phase.

The average grain size of a bainite phase and a martensitic phase isacquired by: specifying a bainite phase and a martensite phase by usingan SEM image of a 3.000-fold magnification; assuming each singlecontinuous region as a grain and measuring sizes of grains according toa method specified in JIS G 0552: 1998; and calculating the averagegrain size of the bainite phase and the martensite phase, respectively,by converting the obtained grain sized thereto.

(2) Tensile Property

For each steel sheet sample, a No. 5 type test piece as specified in JISZ 2001, having a longitudinal direction (tensile direction) orthogonalto the rolling direction, is prepared. A tensile test according to JIS Z2241 is then performed by using the No. 5 type test piece forevaluation.

(3) Bendability (Limit Bending Radius)

Bendability is evaluated according to the V-block method as specified inJIS Z 2248. In the evaluation, generation of cracks at the outer side ofa bent portion is visually observed and the minimum bending radius whichallows bending without generating a crack is regarded as the limitbending radius. When the limit bending radius is equal to or smallerthan 0.3t, it is judged that the bendability is good. Note that Table 4shows values of the limit bending radius/t, as well.

(4) Weldability (Resistance Spot Welding)

First, spot welding is performed under following conditions:

-   -   Electrode: DR6 mm-40R;    -   Welding pressure: 4802 N (490 kgf);    -   Initial press time: 30 cycles/60 Hz;    -   Weld Time: 17 cycles/60 Hz; and    -   Retention Time: 1 cycle/60 Hz.

Test current is changed at 0.2 kA intervals from 4.6 to 10 kA and at 0.5kA intervals from 10.5 kA to the welding, respectively, for the steelsheet having the same sample number.

Next, each test piece is subjected to a cross-tension test andmeasurement of nugget diameter at a welded portion. The cross-tensiontest on the resistance spot welded joint is carried out according to JISZ 3137. The measurement of the nugget diameter is carried out accordingto JIS Z 3139.

A half of the plug portion in a symmetrical circular shape afterresistance spot welding is cut along a section perpendicular to thesteel sheet surface and substantially including the center of thewelding point. The cut face is ground, etched and then subjected tooptical microscopic observation of a sectional structure, to therebymeasure a nugget diameter. In Examples, the maximum diameter of a moltenregion from which a corona bond has been excluded is assumed as thenugget diameter.

The welded material having a nugget diameter of 4t^(1/2) (mm) or more issubjected to cross-tension test. In a case where the welded materialexhibits such good welding adhesion as to cause the base material tofracture, the weldability is evaluated as good.

(5) Plane-Bending Fatigue Test

The plane-bending fatigue test is carried out according to JIS Z 2275under a condition of fully alternating stress (stress ratio: 1) at afrequency of 20 Hz. In a case where a durability ratio expressed asfatigue limit/TS is 0.35 or larger, plane-bending fatigue properties areevaluated as good.

TABLE 1 Steel Element Composition (mass %) Symbol C P S Si Mn Al N Cr MoTi Nb B Remarks A 0.051 0.008 0.0008 0.15 2.35 0.035 0.0045 0.95 0.060.045 0.065 0.0013 Steel B 0.099 0.009 0.0009 0.10 2.25 0.040 0.00410.55 0.08 0.042 0.055 0.0012 Steel C 0.085 0.008 0.0008 0.12 2.35 0.0450.0038 0.62 0.10 0.038 0.048 0.0011 Steel D 0.095 0.006 0.0030 0.05 2.150.045 0.0044 0.68 0.12 0.029 0.056 0.0009 Steel E 0.070 0.025 0.00080.05 2.38 0.035 0.0042 0.58 0.08 0.034 0.068 0.0008 Steel F 0.060 0.0270.0007 0.10 2.65 0.040 0.0045 0.53 0.09 0.036 0.072 0.0014 Steel G 0.0850.006 0.0007 0.15 2.30 0.045 0.0038 0.61 0.08 0.021 0.039 0.0009 Steel H0.075 0.009 0.0034 0.25 2.35 0.035 0.0048 0.57 0.09 0.048 0.038 0.0014Steel I 0.105 0.012 0.0015 0.17 2.51 0.045 0.0041 0.74 0.11 0.025 0.0160.0007 Steel J 0.092 0.015 0.0020 0.13 2.42 0.038 0.0037 0.77 0.05 0.0230.020 0.0005 Steel K 0.087 0.017 0.0017 0.12 2.32 0.055 0.0020 0.82 0.030.014 0.027 0.0012 Steel L 0.110 0.009 0.0025 0.24 2.01 0.027 0.00290.87 0.12 0.012 0.035 0.0010 Steel M 0.082 0.008 0.0012 0.22 2.09 0.0530.0024 0.52 0.15 0.017 0.041 0.0011 Steel N 0.125 0.006 0.0007 0.05 2.250.050 0.0048 0.55 0.08 0.035 0.055 0.0012 Comparative Steel O 0.0950.007 0.0009 0.05 2.70 0.045 0.0042 0.15 0.08 0.034 0.051 0.0014 Steel P0.085 0.008 0.0008 0.15 2.70 0.045 0.0045 0.75 0.08 0.031 — 0.0009 SteelQ 0.052 0.009 0.0008 0.01 3.65 0.040 0.0039 0.52 0.01 0.021 0.031 0.0008Steel R 0.112 0.010 0.0020 0.09 2.22 0.030 0.0037 0.67 0.09 — 0.0210.0009 Steel S 0.115 0.050 0.0040 0.08 2.76 0.044 0.0037 0.72 0.11 0.0130.015 0.0016 Comparative Steel T 0.118 0.014 0.0100 0.11 3.30 0.0410.0042 0.90 0.01 0.016 0.021 0.0014 Comparative Steel U 0.101 0.0120.0008 0.3 3.35 0.030 0.0034 — — — — — Steel V 0.109 0.011 0.0009 0.243.18 0.038 0.0029 — — — — — Steel W 0.113 0.009 0.0013 0.25 2.74 0.0320.0035 0.51 — — — — Steel X 0.089 0.016 0.0018 0.18 2.88 0.031 0.0033 —0.14 — — — Steel Y 0.093 0.017 0.0020 0.11 2.62 0.040 0.0028 — — — —0.0015 Steel Z 0.074 0.013 0.0024 0.08 2.54 0.025 0.0037 0.78 0.28 — —0.0010 Steel ZA 0.098 0.008 0.0019 0.14 3.02 0.028 0.0026 — — 0.071 —0.0003 Steel ZB 0.118 0.010 0.0020 0.27 2.94 0.034 0.0041 — — — 0.074 —Steel ZC 0.105 0.014 0.0027 0.22 2.74 0.027 0.0039 — — 0.072 0.0650.0003 Steel ZD 0.103 0.015 0.0016 0.13 2.42 0.036 0.0034 0.84 — 0.0420.036 — Steel ZE 0.092 0.011 0.0010 0.23 3.14 0.030 0.0029 — — 0.049 — —Steel

TABLE 2-1 Average Cooling Excess Rate Primary Air Slab Finishing FromAverage Ratio Heating Rolling Finishing Coiling Heating IntermediateDuring Steel Temperature Temperature Temperature Temperature RateTemperature Primary No. Symbol (° C.) (° C.) (° C./sec) (° C.) (°C./sec.) (° C.) Heating 1 A 1280 900 25 620 15 650 1.15 2 B 1270 890 50530 20 670 1.12 3 B 1270 890 50 530 20 670 1.08 4 B 1270 890 50 530 20670 1.25 5 C 1250 880 75 510 25 670 1.18 6 D 1210 870 95 570 35 750 1.187 E 1170 910 135  530 10 650 1.13 8 F 1250 930 120  510 25 600 1.15 9 G1250 890 75 500 20 700 1.15 10 G 1250 890 75 500 20 700 1.05 11 G 1250890 75 500 20 700 1.22 12 H 1180 870 85 560 35 640 1.17 13 I 1230 910 20420  5 700 1.18 14 J 1200 920 30 530 30 520 1.11 15 K 1180 900 60 460 25750 1.10 16 L 1160 920 70 550 15 600 1.17 17 M 1200 930 40 490 12 6601.16 18 G 1350 900 95 570 25 710 1.15 19 G 1200 910  3 600 15 700 1.1520 G 1200 910 50 700 15 700 1.14 21 G 1210 920 80 600  3 790 1.16 22 G1200 910 50 550 20 820 1.13 23 G 1180 900 95 590 20 800 1.11 24 G 1170900 85 570 15 780 1.18 25 G 1280 900 80 550 20 740 1.19 26 G 1250 880 95530 35 700 1.15 27 G 1280 890 85 510 20 720 1.12 28 N 1230 900 110  56035 740 1.15 29 O 1210 910 90 550 25 720 1.11 30 P 1180 930 85 530 15 7001.14 Secondary Average Average Cooling Heating Annealing RetentionCooling Stop Skin- Rate Temp. Time Rate Temp. Alloying pass No. (°C./sec.) (° C.) (sec) (° C./sec.) (° C.) Status (%) Remarks  1 0.5 82525  5 515 Alloyed 0.3 Example  2 0.4 820 35  7 525 Alloyed 0.3 Example 3 0.4 820 35  7 525 Alloyed 0.3 Comparative Example  4 0.4 820 35  7525 Alloyed 0.3 Comparative Example  5 0.3 820 45  9 510 Alloyed 0.3Example  6 0.1 825 200  25 495 Alloyed 0.3 Example  7 0.5 835 45 30 505Alloyed 0.3 Example  8 0.7 820 40 20 515 Alloyed 0.3 Example  9 5.5 83050 10 480 Alloyed 0.3 Example 10 5.5 830 50 10 480 Alloyed 0.3Comparative Example 11 5.5 830 50 10 480 Alloyed 0.3 Comparative Example12 3.5 815 110  20 495 Alloyed 0.3 Example 13 1.4 850 50 15 500 Non- 0.3Example Alloyed 14 3.2 770 150  10 520 Alloyed 0.3 Example 15 0.6 860 9020 495 Alloyed 0.3 Example 16 0.9 780 180   8 510 Alloyed 0.3 Example 171.2 800 100  10 460 Non- 0.3 Example Alloyed 18 2.4 830 85  7 500Alloyed 0.3 Comparative Example 19 1.5 800 90 10 490 Alloyed 0.3Comparative Example 20 1.5 800 90 15 500 Alloyed 0.3 Comparative Example21 0.1 830 65 20 485 Alloyed 0.3 Comparative Example 22 1.5 880 120  10510 Alloyed 0.3 Comparative Example 23 15.0  835 45 15 495 Alloyed 0.3Comparative Example 24 0.5 950 55 12 505 Alloyed 0.3 Comparative Example25 1.5 830 600  10 515 Alloyed 0.3 Comparative Example 26 2.5 825 45  0.3 495 Alloyed 0.3 Comparative Example 27 3.5 830 35  8 570 Alloyed0.3 Comparative Example 28 0.6 830 35 15 520 Alloyed 0.3 ComparativeExample 29 0.9 825 45 20 495 Alloyed 0.3 Example 30 1.6 835 55 15 505Alloyed 0.3 Example

TABLE 2-2 Average Cooling Primary Excess Rate Average Ai Slab FinishingFrom Temp. Ratio Heating Rolling Finishing Coiling Rise IntermediateDuring Steel Temperature Temperature Temperature Temperature RateTemperature Primary No. Symbol (° C.) (° C.) (° C./sec) (° C.) (°C./sec) (° C.) Heating 31 Q 1170 920 75 560 20 680 1.13 32 R 1220 900 55510 20 620 1.12 33 S 1250 900 30 570 15 560 1.11 34 T 1200 900 45 420 5640 1.18 35 U 1170 910 30 620 20 600 1.12 36 V 1230 900 50 630 30 6501.14 37 W 1150 890 70 600 15 620 1.16 38 X 1200 880 100 540 10 700 1.1339 Y 1180 900 60 500 35 630 1.12 40 Z 1200 940 50 520 25 540 1.18 41 ZA1290 930 80 550 15 570 1.17 42 ZB 1230 940 60 600 45 600 1.11 43 ZC 1270920 70 620 20 580 1.13 44 ZD 1250 930 30 580 15 630 1.15 45 ZE 1240 91040 610 12 650 1.14 Secondary Average Average Cooling Heating AnnealingRetention Cooling Stop Skin- Rate Temp. Time Rate Temp. Alloying passNo. (° C./sec.) (° C.) (sec) (° C./sec) (° C.) Status (%) Remarks 31 2.6830 65 20 515 Alloyed 0.3 Example 32 0.8 860 80 12 505 Alloyed 0.3Example 33 1.8 830 40 12 485 Alloyed 0.3 Comparative Example 34 3.8 82060 25 470 Alloyed 0.3 Comparative Example 35 0.8 780 60 10 480 Alloyed0.3 Example 36 1.9 820 80 7 500 Alloyed 0.3 Example 37 3.1 880 90 5 510Alloyed 0.3 Example 38 2.6 800 100 15 460 Alloyed 0.3 Example 39 2.7 760120 20 530 Alloyed 0.3 Example 40 1.5 825 80 18 470 Alloyed 0.3 Example41 1.3 850 30 20 500 Alloyed 0.3 Example 42 0.6 840 60 30 490 Alloyed0.3 Example 43 1.1 800 20 14 520 Alloyed 0.3 Example 44 0.7 830 50 10515 Non- 0.3 Example Alloyed 45 0.9 820 180 15 480 Alloyed 0.3 Example

TABLE 3-1 Volume Fraction Of Ferrite in Steel Steel Sheet Structure from10 to 50 μm Steel Sheet Structure Sheet depth measured from Steel SheetSurface at a ¼ Sheet Thickness position Surface Bainite Phase BainitePhase Layer and/or and/or (to Martensitic Remaining Martensitic 10 μmFerrite Phase Phase Remaining Structure* Phase Remaining depth) AverageAverage Structure* Average Average Structure* Volume Grain Volume GrainVolume Volume Grain Volume Grain Volume Volume Steel Fraction SizeFraction Size Fraction Fraction Size Fraction Size Fraction Fraction NoSymbol (%) (μm) (%) (μm) (%) (%) (μm) (%) (μm) (%) (%) Remarks 1 A 953.2 48 1.9 51 1 2.9 42 1.9 56 2 Example 2 B 82 3.0 47 2.1 53 0 2.8 432.2 56 1 Example 3 B 64 3.2 49 2.0 51 0 2.8 43 2.2 56 1 ComparativeExample 4 B 99 5.4 72 2.1 28 0 2.8 43 2.2 56 1 Comparative Example 5 C95 2.1 41 2.7 56 3 1.8 37 2.6 59 4 Example 6 D 96 2.1 46 2.8 51 3 1.7 432.7 55 2 Example 7 E 84 1.8 46 3.1 53 1 1.6 42 2.9 58 0 Example 8 F 902.0 50 1.9 48 2 2.1 46 2.0 54 0 Example 9 G 97 3.2 47 2.4 52 1 2.8 432.5 55 2 Example 10 G 57 3.2 47 2.4 52 1 2.8 43 2.5 55 2 ComparativeExample 11 G 99 5.2 76 2.5 24 0 2.8 43 2.5 55 2 Comparative Example 12 H87 3.6 46 2.7 54 0 3.4 45 2.7 55 0 Example 13 I 83 4.3 35 3.8 63 2 4.031 3.7 65 4 Example 14 J 79 3.8 51 3.0 47 2 3.5 48 3.1 51 1 Example 15 K76 3.2 42 2.6 57 1 2.9 40 2.6 60 0 Example 16 L 94 2.1 55 1.9 44 1 1.853 1.9 46 1 Example 17 M 90 2.4 48 2.8 48 4 2.2 45 2.6 53 2 Example 18 G85 8.2 47 10.9  50 3 7.8 43 10.6  55 2 Comparative Example 19 G 86 8.849 7.9 51 0 8.6 45 7.8 54 1 Comparative Example 20 G 82 7.1 49 6.3 50 16.8 46 6.4 52 2 Comparative Example 21 G 88 6.1 46 7.0 54 0 5.9 43 6.956 1 Comparative Example 22 G 81 5.9 41 8.4 56 3 5.8 38 8.3 61 1Comparative Example 23 G 80 1.9 78 3.9 20 2 1.6 76 4.0 26 0 ComparativeExample *Residual Austenite Phase and/or Pearlite Phase

TABLE 3-2 Steel Sheet Structure to the depth of 10 to 50 μm Steel SheetStructure at a position Volume from Steel Sheet Surface of ¼ SheetThickness Fraction Bainite Phase Bainite Phase of Ferrite in and/orand/or Steel Sheet Martensitic Remaining Martensitic Surface FerritePhase Phase Remaining Structure* Phase Remaining Layer to AverageAverage Structure* Average Average Structure* 10 μm Grain Volume GrainVolume Volume Grain Volume Grain Volume Volume Volume Size Fraction SizeFraction Fraction Size Fraction Size Fraction Fraction No Steel SymbolFraction (%) (μm) (%) (μm) (%) (%) (μm) (%) (μm) (%) (%) Remarks 24 G 927.7 33 10.8  67 0 7.5 28 10.8  72 0 Comparative Example 25 G 94 6.9 467.1 51 3 6.8 43 7.2 53 4 Comparative Example 26 G 92 3.2 75 3.5 16 9 2.972 3.5 18 10  Comparative Example 27 G 88 3.0 47 4.3 42 11  2.7 45 4.243 12  Comparative Example 28 N 86 1.9 46 2.5 53 1 1.7 44 2.4 56 1Comparative Example 29 O 77 3.1 44 2.4 56 0 2.9 41 2.3 58 0 Example 30 P90 2.9 47 4.8 51 2 2.6 43 4.8 57 3 Example 31 Q 94 2.4 40 4.7 57 3 2.237 4.7 60 2 Example 32 R 86 4.9 44 4.5 55 1 4.7 42 4.5 58 0 Example 33 S79 4.5 48 4.4 52 0 4.3 44 4.6 54 2 Comparative Example 34 T 90 3.4 383.6 60 2 3.2 35 3.8 62 3 Comparative Example 35 U 75 3.9 55 3.3 43 2 3.553 3.2 46 1 Example 36 V 82 4.2 57 3.8 42 1 4.0 55 3.5 43 2 Example 37 W88 4.8 46 4.0 51 3 4.4 42 3.8 55 3 Example 38 X 94 4.0 53 4.1 46 1 3.651 3.9 48 1 Example 39 Y 77 3.7 60 3.6 40 0 4.0 57 3.5 43 0 Example 40 Z82 4.2 60 4.0 40 0 3.9 58 3.9 41 1 Example 41 ZA 79 3.3 54 3.3 43 3 3.052 3.0 46 2 Example 42 ZB 76 3.4 48 3.3 50 2 3.2 44 3.1 54 2 Example 43ZC 85 3.2 49 3.1 48 3 3.2 48 3.0 50 2 Example 44 ZD 87 3.1 52 3.1 46 23.0 50 3.1 49 1 Example 45 ZE 81 3.3 62 3.2 38 0 3.2 61 3.2 38 1 Example*Residual Austenite Phase and/or Pearlite Phase

TABLE 4 Material Properties Limit Bending Steel YP/ TS/ Radius/SheetResistance Spot Durability No Symbol MPa MPa El/% Thickness WeldabilityRatio Remarks 1 A 703 1008 15.1 0.13 Base Material Fracture 0.40 Example2 B 717 1035 14.6 0.25 Base Material Fracture 0.41 Example 3 B 714 103214.7 0.75 Base Material Fracture 0.41 Comparative Example 4 B 658 101615.1 0.13 Base Material Fracture 0.32 Comparative Example 5 C 731 105213.4 0.13 Base Material Fracture 0.40 Example 6 D 700 1030 14.6 0.13Base Material Fracture 0.41 Example 7 E 703 1004 15.0 0.25 Base MaterialFracture 0.40 Example 8 F 742 1060 14.3 0.13 Base Material Fracture 0.39Example 9 G 685 1022 14.7 0.13 Base Material Fracture 0.41 Example 10 G695 1026 14.8 0.50 Base Material Fracture 0.41 Comparative Example 11 G624  994 15.1 0.13 Base Material Fracture 0.31 Comparative Example 12 H720 1044 13.9 0.25 Base Material Fracture 0.36 Example 13 I 732 106116.3 0.13 Base Material Fracture 0.37 Example 14 J 704 1009 16.7 0.25Base Material Fracture 0.41 Example 15 K 711 1030 15.0 0.25 BaseMaterial Fracture 0.38 Example 16 L 738 1025 14.7 0.13 Base MaterialFracture 0.41 Example 17 M 674 1048 16.2 0.25 Base Material Fracture0.39 Example 18 G 715 1022 14.7 0.75 Base Material Fracture 0.35Comparative Example 19 G 692 1013 13.4 0.75 Base Material Fracture 0.36Comparative Example 20 G 683 1002 14.0 0.75 Base Material Fracture 0.38Comparative Example 21 G 686 1024 14.7 0.50 Base Material Fracture 0.37Comparative Example 22 G 765 1084 11.3 1.00 Base Material Fracture 0.38Comparative Example 23 G 556  814 19.5 0.13 Base Material Fracture 0.40Comparative Example 24 G 819 1170 10.1 0.75 Base Material Fracture 0.35Comparative Example 25 G 711 1015 14.8 0.50 Base Material Fracture 0.36Comparative Example 26 G 540  771 19.2 0.13 Base Material Fracture 0.35Comparative Example 27 G 715  905 17.8 0.13 Base Material Fracture 0.35Comparative Example 28 N 784 1120 11.2 0.13 Fracture in Nugget 0.41Comparative Example 29 O 682  995 10.1 0.30 Base Material Fracture 0.40Example 30 P 722 1032 14.6 0.30 Base Material Fracture 0.39 Example 31 Q759 1084 11.8 0.30 Base Material Fracture 0.39 Example 32 R 625  99116.1 0.30 Base Material Fracture 0.38 Example 33 S 605 1014 16.5 0.25Fracture in Nugget 0.39 Comparative Example 34 T 764 1082 14.1 0.25Fracture in Nugget 0.40 Comparative Example 35 U 683 1046 16.1 0.30 BaseMaterial Fracture 0.36 Example 36 V 716 1024 14.8 0.30 Base MaterialFracture 0.35 Example 37 W 843 1094 10.5 0.30 Base Material Fracture0.35 Example 38 X 643 1001 16.8 0.30 Base Material Fracture 0.36 Example39 Y 635  983 17.0 0.30 Base Material Fracture 0.37 Example 40 Z 608 989 17.2 0.30 Base Material Fracture 0.38 Example 41 ZA 712 1036 15.10.30 Base Material Fracture 0.38 Example 42 ZB 746 1088 13.4 0.30 BaseMaterial Fracture 0.39 Example 43 ZC 772 1062 12.1 0.30 Base MaterialFracture 0.38 Example 44 ZD 693 1041 14.2 0.30 Base Material Fracture0.39 Example 45 ZE 706  999 16.5 0.30 Base Material Fracture 0.38Example

As shown in Table 4, our high strength galvanized steel sheets exhibitexcellent bend-ability (the limit bending radius ≦0.3t) and excellentresistance spot weldability, while simultan-eously satisfying good planebending fatigue properties (durability ratio ≧0.35). Further, it isunderstood that the Examples with the steel symbols A to M eachsatisfying a particularly prefer-able composition reliably exhibit moreexcellent bendability (the limit bending radius ≦0.25t).

In contrast, the steel samples of No. 28, 33, and 34, each having asteel element composition beyond our range, exhibit relatively poorweldability, respectively.

The steel samples of No. 3, 4, 10, and 11, each having an excess airratio during the primary heating beyond our range, exhibit relativelypoor bendability or plane-bending fatigue properties (durability ratio),respectively.

The steel samples of No. 18, 21, and 25, in each of which at least oneof the conditions of the slab heating temperature, the primary heatingrate, and the retention time is beyond our range(s), exhibit relativelypoor bendability, respectively, because the crystal grain size of theferrite phase is coarse.

The steel sample of No. 19, having the average cooling rate from thefinishing temperature beyond our range, exhibits relatively poorbendability because the crystal grain size of the ferrite phase iscoarse.

The steel samples of No. 20 and 22, each having the coiling temperatureand the intermediate temperature beyond our ranges, exhibit relativelypoor bendability, respectively, because the crystal grain size of theferrite phase is coarse.

The steel samples of No. 23 and 26, each having the secondary heatingrate or the cooling rate to the cooling stop temperature beyond ourrange, exhibit a relatively large volume fraction of the ferrite phaseand thus a TS value lower than 980 MPa, respectively.

The steel sample of No. 24, having the annealing temperature beyond ourrange, exhibits relatively poor bendability because the crystal grainsize of the ferrite phase is coarse.

The steel sample of No. 27 having the cooling stop temperature beyondour range exhibits TS lower than 980 MPa.

INDUSTRIAL APPLICABILITY

Our high strength galvanized steel sheets have excellent bendability andweldability, as well as a high tensile strength, and therefore can besuitably used, to cause a good effect, for applications requiring strictdimensional accuracy and bendability such as automobile components,architecture and household appliances.

1. A high strength galvanized steel sheet having excellent bendabilityand weldability, comprising by mass %: C: equal to or more than 0.05%and less than 0.12%; P: 0.001 to 0.040%; and S: equal to or less than0.0050%, wherein a steel sheet surface layer, constituting a portion ofthe steel sheet up to a depth of 10 μm measured from each surface of thesteel sheet, has a structure containing more than 70% of ferrite phaseby a volume fraction, a steel sheet inner layer portion, on an innerside than the depth of 10 μm measured from each surface, has a structurecontaining 20 to 70% by a volume fraction of ferrite phase with anaverage crystal grain size equal to or smaller than 5 μm, the steelsheet has a tensile strength equal to or larger than 980 MPa, and thesteel sheet has a galvanized layer on a surface thereof.
 2. The steelsheet of claim 1, wherein the structure of the steel sheet inner layerportion contains: 20 to 70% of ferrite phase by a volume fraction, withan average crystal grain size equal to or smaller than 5 μm; 30 to 80%of bainite phase and/or martensitic phase by a volume fraction, with anaverage crystal grain size of equal to or smaller than 5 μm; andresidual austenite phase and/or pearlite phase equal to or less than 5%(inclusive of 0%) by a volume fraction as the remainder.
 3. The steelsheet of claim 1, wherein the steel sheet, further comprises by mass %:C: equal to or more than 0.05% and less than 0.12%; P: 0.001 to 0.040%;S: equal to or less than 0.0050%; Si: 0.01 to 1.6%; Mn: 2.0 to 3.5%; Al:0.005 to 0.1%; N: equal to or less than 0.0060%; and the remainder as Feand incidental impurities.
 4. The steel sheet of claim 3, furthercomprising by mass %: at least one element selected from the groupconsisting of Cr: more than 0.5% and equal to or less than 2.0%, Mo:0.01 to 0.50%, and B: 0.0001 to 0.0030% and the remainder as Fe andincidental impurities.
 5. The steel sheet of claim 3, further comprisingby mass %: at least one element selected from the group consisting ofTi: 0.010 to 0.080% and Nb: 0.010 to 0.080%; and the remainder as Fe andincidental impurities.
 6. The steel sheet of claim 5, comprising by mass%: C: equal to or more than 0.05% and less than 0.12%; P: 0.001 to0.040%; S: equal to or less than 0.0050%; Si: 0.01 to 1.6%; Mn: 2.0 to3.5%; Al: 0.005 to 0.1%; N: equal to or less than 0.0060%; Cr: more than0.5% and equal to or less than 2.0%; Mo: 0.01 to 0.50%; Ti: 0.010 to0.080%; Nb: 0.010 to 0.080%; B: 0.0001 to 0.0030%; and the remainder asFe and incidental impurities.
 7. A method of manufacturing a galvanizedsteel sheet comprising: subjecting a steel slab having a compositionaccording to claim 1 to heating at a temperature of 1150° C. to 1300° C.and then hot rolling the slab at a hot finishing rolling temperature of850 to 950° C. to form a steel sheet; cooling the steel sheet from thehot finishing rolling temperature to (the hot finishing rollingtemperature minus 100° C.) at an average cooling rate of 5 to 200°C./second; winding up the steel sheet into a coil at a temperature of400 to 650° C.; subjecting the steel sheet to pickling and cold rolling;and subjecting the steel sheet to annealing including a two-stagetemperature raising processes, wherein the annealing step includes:primary heating the steel sheet from 200° C. to an intermediatetemperature of 500 to 800° C. at a primary average heating rate of 5 to50° C./second at an excess air ratio of 1.10 to 1.20 maintained up tothe intermediate temperature; secondary heating the steel sheet from theintermediate temperature to an annealing temperature of 730 to 900° C.at a secondary average heating rate of 0.1 to 10° C./second at an excessair ratio of less than 1.10 maintained up to the annealing temperature;holding the steel sheet in a range of the annealing temperature for 10to 500 seconds; cooling the steel sheet to a temperature of 450 to 550°C. at an average cooling rate of 1 to 30° C./second; and subjecting thesteel sheet to a galvanizing process and optionally, an alloyingprocess.
 8. The steel sheet of claim 2, wherein the steel sheet, furthercomprises by mass %: C: equal to or more than 0.05% and less than 0.12%;P: 0.001 to 0.040%; S: equal to or less than 0.0050%; Si: 0.01 to 1.6%;Mn: 2.0 to 3.5%; Al: 0.005 to 0.1%; N: equal to or less than 0.0060%;and the remainder as Fe and incidental impurities.
 9. The steel sheet ofclaim 8, further comprising by mass %: at least one element selectedfrom the group consisting of Cr: more than 0.5% and equal to or lessthan 2.0%, Mo: 0.01 to 0.50%, and B: 0.0001 to 0.0030% and the remainderas Fe and incidental impurities.
 10. The steel sheet of claim 4, furthercomprising by mass %: at least one element selected from the groupconsisting of Ti: 0.010 to 0.080% and Nb: 0.010 to 0.080%; and theremainder as Fe and incidental impurities.
 11. The steel sheet of claim9, further comprising by mass %: at least one element selected from thegroup consisting of Ti: 0.010 to 0.080% and Nb: 0.010 to 0.080%; and theremainder as Fe and incidental impurities.